Research into Grinding Hardening of Microalloyed Non-quenched and Tempered Steel

Grinding hardening is a new technology of hardening steel piece surfaces with grinding heat generated in the grinding process instead of with a high or medium frequency induction heating method,which can effectively integrate grinding and surface hardening. Experimental studies were carried out on grinding hardening of non-quenched and tempered steel. Through grinding experiments with variable depths of cut and feeding rate,the variation in the depth of the hardening layer was studied and the microstructure of the hardening zone of the test pieces was subsequently ana-lyzed. In the end,the hardening effect of non-quenched and tempered steel was compared with that of 40Cr steel,which revealed the superiority of non-quenched and tempered steel in grinding hardening technology.

Development of non-quenched and tempered bolt steel

The 8.8 grade non-quenched and tempered bolt steel was studied according to the process conditions of wire rod plant and customer requirments.Three types of experimental steel grades were selected.10MnSiTi Nb and 20Mn2VTi(N) were chosen as the formal steel after several experimemts.

Effects of low-temperature tempering on the microstructure and precipitating evolution of newly developed high-strength microalloyed steel

The effect of tempering temperature on the microstrocture and precipitating evolution and the resultant mechanical properties of newly developed high-strength microalloyed steel plate was investigated by optical microscopy （OM） and transmission electron microscopy （TEM）. The steel mainly consists of fine lath martensite and lower bainite. The width of the martensitic laths in as-hot-rolled state is about 120 nm,and increases from 120 nm to 150 nm and 180 nm after tempering at 200 ℃ and 250℃ for 2 h respectively with no change in its morphology. Of special interest is the phenomenon that both tensile strength and impact toughness of the steel plate decrease with the increase of the tempering temperature, which might be attributed to the combination of lath martensite broadening and the coarsening of needle-like carbides located on the boundaries of lath martensite and within bainitic ferrite. It is suggested that the existence of the complex carbonitride larger than 100 nm in bainitic ferrite is one of the reasons.

Theoretical calculation of the impact work in the alloying non-quenched and tempered steel

Coupled with hot-continuous rolling technology and based on the calculation of the finishing rolling impact work in the non-quenched and tempered Si-Mn steel, the calculations of the finishing rolling impact work in the alloying non-quenched and tempered steel with the elements of Cr, Ni, Mo, W, Cu, V, Nb and Ti are studied with the covalent electron number nA of the strongest bond in alloying phases, the smallest electron density difference ?ρ of phase interfaces, and the number of atom states σ (σ′) which keep the interface electron density continuous. The calculated results show that the finishing rolling impact work of the alloying non-quenched and tempered steel intensely depends on strengthening mechanisms. The solution strengthening, interface strengthening, precipita- tion strengthening of pearlite, and dispersion strengthening will result in the decrease of the finishing rolling impact work; the refinement strengthening, the precipitation strength- ening of V, Nb and Ti in α-Fe-C-V(Nb, Ti), and the residual austenite containing Ni on the boundary of α-Fe-C-Ni will increase the impact work; and the increments or decrements can be calculated with nA, ?ρ, σ (σ′) and weights of alloying elements. The calculation formulas of the finishing rolling impact work in this paper are intergraded with the sug- gested ones of the finishing rolling tensile strength, yield strength, and elongation of the non-quenched and tempered steel. The calculated results agree well with the measured ones.

Theoretical calculation of the finishing rolling impact work in non-quenched and tempered Si-Mn steel

Based on the hot-continuous rolling technology, the finishing rolling impact work α k of the non-quenched and tempered Si-Mn steel is theoretically calculated with the covalent electron number nA of the strongest bond in alloying phases, and the smallest interface electron density difference Δρ of alloying phase interface and the number of atom states σ which keep the interface electron density continuous. Calculations show that the solution strengthening, the precipitation strengthening, and the interface strengthening will result in the decrease of the finishing rolling impact work α k, and the effects of the number of atom states σ which keep the interface electron density continuous on the finishing rolling impact work α k are different. Taking the impact work and the number of atom states σ 0 keeping the electron density continuous of the phase interface α-Fe/α-Fe-C between α-Fe and α-Fe-C as reference values, the impact work of the interface will increase when σ of some interface is larger than σ 0; otherwise, the impact will decrease. Therefore, the finishing rolling impact work α k can be calculated with the impact value of the refined α-Fe matrix and the influence amounts caused by the solution strengthening, the precipitation strengthening, the interface strengthening, and the number of atom states σ which keep the interface electron density continuous. The calculated results agree well with the measured ones. In this paper, the effect of S on the impact work is also discussed.

Effect of Nb-V Microalloying on Microstructures and Mechanical Properties of Medium Carbon Non-Quenched and Tempered Steel

Based on optical microscope(OM),transmission electron microscope(TEM) and mechanical performance measurement,the microstructures and mechanical properties of Nb-V micro-alloying non-quenched and tempered steels have been studied.The results showed that the microstructure consists of ferrite and pearlite,in which there exists a lot of intragranular ferrite.Niobium carbide is the main form of carbonitrides,Nb-enriched carbonitrides refine grains,V-enriched carbonitrides have precipitation strengthening effect,which promotes the toughness of the studied steel.The mechanical properties for steels 1,2 and 3 have met the standards required by high load automobile crankshaft,in which the comprehensive property for No.2 is the best.

Morphological transformation of elongated MnS inclusions in non-quenched and tempered steel during isothermal heating

Elongated MnS inclusions in rolled non-quenched and tempered steel tend to cause the mechanical anisotropy of steel,deteriorate the mechanical properties and degrade the quality and service life of the steel products.To reveal the mechanisms of morphological transformation of strip-shaped MnS inclusions during isothermal heating,the effects of heat treatment time and temperature on the morphology,number density and size distribution of elongated MnS inclusions were systematically studied and discussed.A diffusion couple experiment was also conducted to clarify the diffusion mode of MnS inclusions.The experimental results showed that with the increase in isothermal heating time(from 0 to 10 h at 1473 K)and temperature(from 1173 to 1573 K for 3.0 h),the number density and average aspect ratio of MnS inclusions generally showed an increase and decrease trend,respectively,while the area fraction remained stable and only slightly fluctuated around 0.4%.In the diffusion couple,after the isothermal heating at 1473 K for 3.0 h,the elements Mn and S in the steel near the steel-MnS interface were very stable without any concentration gradient.The morphology change sequence of the elongated MnS inclusions in the rolled non-quenched and tempered steel during the isothermal heating was strip→cylinderization→spindle→spheroidization.Relationship between the diameter of MnS inclusion and the spacing between two MnS inclusions after splitting,and the fitting goodness of different n values under different experimental time and temperature confirmed that the driving force for the transformation of MnS inclusions during the isothermal heating was surface diffusion,instead of volume diffusion.

Review on regulation of MnS in non-qquenched and tempered steel

An overview of the current research status and control methods of MnS in non-quenched and tempered steel was provided.As a low-melting plastic inclusion,the morphology and distribution of MnS were influenced by various production processes.Therefore,control of MnS is a systematic problem that must be integrated into the entire production process.Based on the production process,the factors affecting the morphology and distribution of MnS in steel were introduced.The effects of oxygen activity,manganese,sulfur,and some alloys on MnS inclusion precipitation were summarized,mainly including MnS modification treatment and oxygen-sulfide composite precipitation control.It is believed that MnS precipitates during the solidification process of steel,and controlling the solidification cooling rate could effectively regulate the size and morphology of MnS,avoiding the precipitation of II-MnS.Additionally,by changing the deformation rate,deformation amount,deformation temperature during the hot deformation process,and heating time and temperature during heat treatment,the distribution and morphology of MnS could be improved.Through the fine control of the above process parameters,the number of II-MnS in steel could be effectively reduced,and their morphology could be improved,thereby enhancing the performance of non-quenched and tempered steel and promoting its wider application.Furthermore,applying laboratory research results to industrial production is an important direction for future research efforts in this field.

Stability of Ultra-fine Microstructures during Tempering

The stability of ultra-fine microstructure during tempering at 650 degreesC was investigated on a Nb-containing steel. The steel had undergone 5 passes controlled rolling, then was relaxed lair cooled) to 730 degreesC: and cooled in water. The evolution of microstructure was that, in early stage of tempering, no obvious change was detected by means of optical microscopy while dislocation cells were formed inside bainitic laths. With further tempering, bainitic laths started to coalesce in some regions. Finally, polygonal ferrite was formed while hardness decreased dramatically. Some samples taken from the same primary plate were reheated at 930 degreesC for 0.5 h followed by quenching into water before tempering. Despite their lower original hardness, the reheated samples softened Faster during tempering. Ferrite was quickly formed in the reheated samples. These results indicate that the evolution of microstructures towards equilibrium during tempering of the steel is mainly determined by whether dislocations are pinned rather than the dislocation density.

Effects of Mg–Ca treatment and Ca treatment on impact toughness and morphology of sulfides in 45MnVS non-quenched and tempered steel

An industrial experiment was conducted at a certain steel plant in China to compare and analyze the effects of Ca treatment and Mg–Ca treatment on inclusions in 45MnVS non-quenched and tempered steel. Through scanning electron microscopy-energy dispersive scanning analysis of the morphology and composition of inclusions, as well as Aspex quantitative analysis of their quantity, type and size, the formation mechanism of MnS–oxide (MnS inclusions with oxide cores) was intensively studied. The influence of sulfide morphology on the impact properties of steel was also analyzed. The results show that the quantity percentage of spindle-shaped sulfides in Ca-treated steel is 19.99%, and that in Mg–Ca-treated steel is 35.38%. Compared with Ca-treated steel, there are more MnS–oxide inclusions in Mg–Ca-treated steel. Controlling the content of Ca and Mg in the oxide core of MnS–oxide inclusion above 10 wt.% and the area ratio below 5 would contribute to the formation of spindle-shaped inclusions after rolling. The mismatch between MnS and oxides decreases with the increase in MgO content in the oxides, which is beneficial to nucleation and precipitation of MnS with this type of oxides as the core. Under the same deformation conditions, the size of sulfide does not affect its aspect ratio. Under the experimental conditions, the inclusion containing a certain amount of MgO can enhance its sulfur capacity, facilitating the formation of composite sulfides. The transverse impact energy of Ca-treated steel is 25.785 J, and that of Mg–Ca-treated steel is 32.119 J. Compared with the traditional Ca-treatment, Mg–Ca treatment can increase the number of spindle-shaped sulfides in the steel, thereby improving the transverse impact toughness of the steel and reducing the anisotropy of the mechanical properties of the material.

Estimation of probable maximum aspect ratio of MnS inclusions in non-quenched and tempered steel after isothermal compression

To clarify the deformation behavior of MnS inclusions in a non-quenched and tempered steel at three different positions (edge, 1/2 radius and center) in the cross-section of the billet in the course of hot rolling, isothermal compression experiments were performed under the deformation temperature range from 1073 to 1473 K, the reduction rates from 25% to 75% and the strain rates from 0.01 to 10 s^(−1). The variations of deformability features (i.e., aspect ratios, size distributions, and morphologies) of MnS inclusions with those isothermal compression parameters were revealed. The evaluation of the probable maximum aspect ratio of MnS inclusions at the three different positions in the cross-section of the billet after hot rolling was examined using the statistical analysis of extreme values. Results showed that the number densities of MnS inclusions at three different positions (edge, 1/2 radius and center) in the cross-section of the steel billet only fluctuated slightly when the deformation parameters varied in the isothermal compression, while the average inclusion aspect ratios in all cases generally have a negative correlation with the deformation temperature and positive correlations with the reduction ratio and the strain rate. Statistical analysis reveals that larger inclusions deform more easily during hot rolling. The effect of rolling temperature on the extreme value of the aspect ratio of inclusions is the smallest, while the effects of initial size, reduction ratio and strain rate are more significant.

非调质27CrMn2VS钢的开发及工业生产实践

非调质钢由于市场的需要而在机械、汽车、风电等领域得到广泛应用,在欧美和日本等发达国家的非调质钢生产水平成熟且应用普及率较高,但在中国发展较晚、应用率偏低且进口率高。通过对化学成分、生产工艺流程(80 t转炉→LF精炼→VD真空→连铸)的设计,得到了一种工程机械用非调质27CrMn2VS钢(/%:0.22~0.35 C,0.20~0.40 Si,1.50~2.50 Mn,0.035~0.065 S,0.35~0.65 Cr,0.05~0.15 V)。工业生产通过使用P≤0.15%,S≤0.35%的铁水、LF精炼3批次喂S线,连铸过程采用电磁搅拌+轻压下的工艺,终轧后轧材入缓冷坑缓冷,获得的显微组织为贝氏体(占比78~88%)+珠光体+铁素体,非金属夹杂物级别A细≤2.5级、A粗≤2.0级、B细≤1.0级、B粗≤1.5级、C类≤0.5级、D类≤0.5级、Ds≤0.5级,屈服强度1020~1050 MPa、抗拉强度820~850 MPa。连续生产5炉的化学成分稳定、洁净度高、内部质量和表面质量极好,可用于替代部分传统'调质钢。

一种汽车用微合金非调质钢的连续冷却转变

测定了一种汽车用微合金非调质钢的过冷奥氏体连续冷却转变曲线,研究了冷却速率对相变组织及显微硬度的影响。结果表明:试验钢的临界点A c3为838℃,A c1为732℃;当冷却速率小于0.2℃/s时,试验钢的连续冷却转变产物为铁素体、珠光体和贝氏体;当冷却速率为0.2℃/s时,转变产物中出现马氏体;当冷却速率为5℃/s时,铁素体、珠光体消失,转变产物为贝氏体和马氏体;随着冷却速率的增大,马氏体含量逐渐增多,贝氏体含量逐渐减少,甚至完全消失;当冷却速率增大至20℃/s时,转变产物均为马氏体;随着冷却速率的增大,试验钢的显微硬度呈先快速增长,后增长速率变缓的趋势。

V-Ti-N微合金非调质无缝油井管钢中碳氮化物的热力学计算

用包括奥氏体γ相和两个碳氮化物相三相溶解度间隙平衡处理的方法计算了V-Ti-N微合金非调质油井管钢中的碳氮化物析出.计算结果表明,此钢奥氏体中的析出模式为1473℃时TiN即开始析出;其后部分TiN逐渐转变为复合(TixV1-x)(CyN1-y)颗粒,而其他的TiN直到低温仍保持其化学性质;最后富V-C的V(CxN1-x)在846℃开始析出.实验数据验证了这种析出模式.计算结果支持了中碳含钒微合金钢中800℃以下奥氏体中的析出对其后的奥氏体分解相变具有明显的调控作用的观点.

Nb-V微合金钢中碳化物析出的三维原子探针表征

将Nb-V微合金钢在1200℃固溶0.5h后淬火,在不同温度回火4h,结合光学显微镜(OM)和透射电子显微镜(TEM),用三维原子探针(3DAP)研究了淬火与回火样品中碳化物的特征.结果显示,淬火样品中V、Nb分布均匀,C由于自回火出现轻微偏聚;450、500、550和600℃回火样品中存在大小和数量不同的V和Nb的碳化物,其中550℃回火样品中数量最高,对应着二次硬化的硬度峰值;650℃回火样品中数量明显减少,与硬度下降对应.

贝氏体型非调质钢的试制

为降低钢结构件的成本,开发了一种新型的贝氏体高强度钢。该钢种属普通低碳合金钢,其特点是以价格较低的V,Mn,Cr取代昂贵的Ni,Mo,B等进行合金化,勿需热处理,生产工艺简单。铸坯的加热和压下制度与其它钢种类似,采用控温轧制和轧后空冷提高钢的强度和韧性。结果表明:试验钢板的抗拉强度较高,均在860MPa以上;且随着终轧温度的提高,钢的冲击韧性得到改善。

33Mn2V油井管用钢奥氏体晶界的显示

利用控温控时水浴锅 ,采用热化学侵蚀法对不同热处理和热机械处理状态 33Mn2V微合金非调质钢奥氏体实际晶粒的金相显示方法进行了研究。结果表明 ,采用自来水 30mL和适量苦味酸并滴加少量盐酸的腐蚀方法可清晰显示 33Mn2V微合金钢奥氏体实际晶粒。晶界显示难易程度与样品状态密切相关 ,晶界线的宽度与首次显示时间有关。

Nb-V复合微合金化中碳非调质钢的连续冷却转变

利用Formastor-Digital膨胀仪测定了Nb-V复合微合金化中碳非调质钢的连续冷却转变曲线（CCT曲线）,并测定了不同冷速下实验钢硬度的变化。分析了不同Nb、V含量对中碳非调质钢连续冷却转变的影响。结果表明,随着Nb、V含量的增加,相变点温度随之降低,并使得转变过程中珠光体、贝氏体转变区域变宽,组织中相应的体积分数增加。冷速在0.08-1℃/s时,组织主要为铁素体和珠光体;当冷速大于2.5℃/s时,开始发生贝氏体转变,随着冷速的进一步增加,贝氏体含量越来越多,并在5℃/s时出现马氏体组织。Nb-V复合微合金化实验钢受冷速的影响较大,随冷速的增大实验钢的显微硬度也随之提高。冷速分别在10℃/s和30℃/s时,硬度突然增大。

C和N含量对V-N-Ti微合金非调质钢组织的影响

研究了C含量0．26wt％～0．42wt％及N含量0．0041wt％～0．021wt％变化对中低碳v—N—Ti微合金非调质钢锻态组织的影响。结果表明，C、N含量对V—N—Ti微合金非词质钢锻态组织中先共析铁素体的数量及分布存在显著影响。钢中的N含量一定，C含量约为0．33wt％时，组织中形成的晶内铁素体数量最多、组织最细小均匀；钢中的C含量一定，锻态组织中先共析铁素体的数量随着N含量的增加而增加，但N含量对先共析铁素体数量的影响要远小于C含量的影响。采用基于经典形核和长大理论模型计算所得析出动力学结果很好地解释了上述现象。

33Mn2V非调质油井管钢的相变特性及其应用

研究了新型热轧非调质无缝油井管用 3 3 Mn2 V钢 ,实验确定了该钢在加热过程和 95 0℃奥氏体化后冷却过程的相变点 ,以及 110 0℃奥氏体化不变形条件下和 12 0 0℃奥氏体化并模拟实际穿管、轧管变形条件下的两种过冷奥氏体连续转变曲线。提出一种不同于业界至今仍普遍认同的观点 ,即“在线常化”技术不是生产 N80钢级非调质热轧油井管必不可少的工艺途径。